JPWO2016031714A1 - Sintered body, tool using the sintered body, and method for manufacturing the sintered body - Google Patents

Abstract

[Problem] To provide a sintered body excellent in wear resistance and fracture resistance and excellent in oxidation resistance. [Means for Solving the Problems] A sintered body containing a first compound composed of Ti, Al, Si, O and N.

Description

  The present invention relates to a sintered body, a tool using the sintered body, and a method for manufacturing the sintered body.

  Conventionally, cutting of steel, castings, and the like has been performed using a tool made of a sintered body. Since the cutting edge of the tool is exposed to a high temperature environment during cutting, the tool is required to have oxidation resistance as well as characteristics such as wear resistance and fracture resistance. As a sintered body expected to have such characteristics, a sintered body made of Ti, Al, and N is known.

For example, Japanese Laid-Open 05-078107 (Patent Document 1), to prepare a powder comprising Ti _0.5 Al _0.5 N with a mechanical alloying (MA) method, which was sintered Ti _{0. 5} Al it is disclosed that the production of sintered bodies consisting of _0.5 N. In Japanese Patent Laid-Open No. 10-182233 (Patent Document 2), a powder made of Ti _1-x Al _x N (x = 0.05 to 0.70) is prepared using a physical vapor deposition (PVD) method. It is disclosed that a titanium nitride aluminum based sintered body is produced by sintering this. JP 2007-131493 (Patent Document 3) uses a combustion synthesis (SHS) method to produce a mixture composed of Ti, Al, and N, and sinters it to produce an Al-added TiN bulk body. It is disclosed.

Japanese Patent Laid-Open No. 05-078107 Japanese Patent Laid-Open No. 10-182233 JP 2007-131493 A

  However, in the sintered body made of Ti, Al and N as described above, it tends to be difficult to improve the required performance in terms of oxidation resistance.

  Accordingly, an object of the present invention is to provide a sintered body excellent in wear resistance and fracture resistance and excellent in oxidation resistance, a tool using the sintered body, and a method for manufacturing the same.

  The sintered body according to one embodiment of the present invention is a sintered body including a first compound composed of Ti, Al, Si, O, and N.

  The tool which concerns on 1 aspect of this invention is a tool using the sintered compact containing the 1st compound which consists of said Ti, Al, Si, O, and N.

  A method for manufacturing a sintered body according to one aspect of the present invention includes a step of preparing first particles containing elements of Ti, Al, and Si, and processing the first particles to obtain Ti, Al, Si, O, and A step of producing second particles comprising each element of N, and a step of producing a sintered body containing the first compound comprising Ti, Al, Si, O and N by sintering the second particles. The step of preparing and producing the second particles includes a step of heating the first particles and a step of rapidly cooling the first particles after heating.

  According to the above, it becomes possible to provide a sintered body excellent in wear resistance and fracture resistance and excellent in oxidation resistance, a tool using the same, and a manufacturing method thereof.

It is a flowchart for demonstrating the manufacturing method of the sintered compact which concerns on 3rd Embodiment. It is a flowchart for demonstrating a process process. It is a flowchart for demonstrating the manufacturing method of the sintered compact which concerns on 4th Embodiment.

[Description of Embodiment of the Present Invention]
First, embodiments of the present invention will be listed and described.

  [1] A sintered body according to an aspect of the present invention includes a first compound composed of Ti, Al, Si, O, and N.

  The first compound composed of Ti, Al, Si, O and N can have a compound composed of Ti, Al, Si, O and N (hereinafter referred to as “TiAlSiON compound”), thereby providing high wear resistance. In addition to high fracture resistance, it can have high oxidation resistance. Therefore, the sintered body according to one embodiment of the present invention can have characteristics such as excellent wear resistance and fracture resistance, and excellent oxidation resistance.

  [2] Preferably, in the sintered body, the first compound is Ti._(1-ab)Al_aSi_bO_xN _yContaining Ti_(1-ab)Al_aSi_bO_xN_yA, b, x and y in the formulas are 0.01 ≦ a ≦ 0.70, 0.01 ≦ b ≦ 0.55, 0.06 ≦ a + b ≦ 0.88, and 0.005 ≦ x ≦ 0. 6, 0.4 ≦ y ≦ 0.995 and 0.5 <x + y ≦ 1 are satisfied. Thereby, a sintered compact is further excellent in the said characteristic.

  [3] In the sintered body, the content of the first compound is preferably 10% by volume or more and 100% by volume or less. When content of the 1st compound in a sintered compact is less than 10 volume%, there exists a tendency for the said characteristic of a sintered compact to fall.

  [4] The sintered body preferably further includes one or more selected from the group consisting of the second compound, the third compound, the fourth compound, and the first metal. The second compound is cubic boron nitride, and the third compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O And the fourth compound is a group consisting of one or more elements selected from the group consisting of Group 4 elements, Group 5 elements and Group 6 elements of the periodic table, and B, C, N, and O The first metal is a compound with one or more elements selected from Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, It is a metal composed of one or more selected from the group consisting of Ta, W and Pb. In this case, the balance of various characteristics of the sintered body is adjusted by appropriately adjusting the composition of each of the second compound, the third compound, the fourth compound, and the first metal and the content ratio in the sintered body. Therefore, a sintered body corresponding to various needs can be provided.

  [5] A tool according to an aspect of the present invention is a tool using the sintered body. Since the sintered body is excellent in characteristics such as wear resistance, fracture resistance and oxidation resistance, a tool using the sintered body can also be excellent in these characteristics. Therefore, the tool according to one embodiment of the present invention can have a longer life than the conventional tool.

  [6] A method for manufacturing a sintered body according to one aspect of the present invention includes a step of preparing first particles containing each element of Ti, Al, and Si, and treating the first particles to obtain Ti, Al, Si. , A step of producing second particles made of each element of O and N, and a step of producing a sintered body containing the first compound made of Ti, Al, Si, O and N by sintering the second particles And the step of producing the second particle includes a step of heating the first particle and a step of rapidly cooling the first particle after heating.

  According to the method for manufacturing a sintered body according to one aspect of the present invention, a sintered body containing a first compound composed of Ti, Al, Si, O, and N can be manufactured. Such a first compound is excellent in properties such as wear resistance, fracture resistance and oxidation resistance, and a sintered body containing the first compound can be excellent in these properties.

  [7] Preferably, the above production method includes a step of mixing the second particles and the third particles before the step of producing the sintered body. The third particles are particles composed of one or more selected from the group consisting of a fifth compound, a sixth compound, a seventh compound, and a second metal. The fifth compound is cubic boron nitride. The sixth compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O. The seventh compound is selected from the group consisting of one or more elements selected from the group consisting of Group 4 elements, Group 5 elements and Group 6 elements in the periodic table, and B, C, N, and O A compound with one or more elements. The second metal is one or more selected from the group consisting of Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, Ta, W, and Pb. It is a metal consisting of In this case, in the sintering step, the mixture of the second particles and the third particles is sintered, and the manufactured sintered body has a desired second compound in addition to the first compound. be able to. For this reason, the balance of the various characteristics of a sintered compact can be adjusted as desired, and the sintered compact corresponding to various needs can be manufactured.

  [8] Preferably, in the manufacturing method, the mixing step is performed with the content of the third particles in the mixed particles of the second particles and the third particles being 90% by volume or more. Thereby, the sintered compact to which the characteristic which the 2nd compound has was added can be manufactured, maintaining the characteristic which the 1st compound has enough.

[Details of the embodiment of the present invention]
Hereinafter, embodiments of the present invention will be described in detail.

In the present specification, the “metal” is not limited to a single metal composed of one kind of metal element such as “Co” unless otherwise specified, and includes two or more kinds such as “CoSi ₂ ”. Includes alloys composed of metal elements. In the present specification, the “compound” refers to a compound composed of one or more metal elements and one or more non-metal elements. In addition, B, C, N, and O are mentioned as a nonmetallic element.

  In addition, when the atomic ratio is not particularly defined in the chemical formulas described in the present specification, the atomic ratio of each element is not necessarily equal, and all conventionally known atomic ratios are included. For example, when describing TiN, the atomic ratio of Ti and N includes 1: 1, and also includes 2: 1, 1: 0.95, 1: 0.9, 1: 0.3, etc. In the description, the atomic ratio of Ti, Zr, and N includes 25:25:50, and all conventionally known atomic ratios are included.

<< First Embodiment >>
The sintered body according to the first embodiment is a sintered body containing a first compound composed of Ti, Al, Si, O, and N. Here, the sintered body is a bulk and has a lump shape, and its shape is different from that of a thin film (film). In addition, the sintered body and the thin film have different shapes, so that not only their characteristics but also their purpose of use and manufacturing method are different. In general, the thickness of the thin film is about 5 μm, and a thin film having a thickness of 100 μm or more cannot be substantially manufactured, whereas the thickness of the sintered body can be 100 μm or more.

  The sintered body containing the first compound composed of Ti, Al, Si, O, and N is a novel one that can be produced by the production method described later, and is a conventional sintered body composed of Ti, Al, and N (hereinafter, The structure is greatly different from that of “TiAlN sintered body”.

  Specifically, the conventional TiAlN sintered body includes a compound composed of Ti, Al and N (hereinafter referred to as “TiAlN compound”). Such a TiAlN compound usually has a structure in which Al is dissolved in a crystal structure composed of Ti and N. On the other hand, the first compound included in the sintered body according to the first embodiment includes a compound composed of Ti, Al, N, Si, and O (hereinafter referred to as “TiAlSiON compound”). This TiAlSiON compound has a structure in which Al, Si and O are further dissolved in a crystal structure composed of Ti and N. Needless to say, the first compound may contain unintended inevitable impurities.

  By including the first compound, the sintered body according to the first embodiment can have not only high hardness and high wear resistance but also high oxidation resistance. This is because the first compound composed of the TiAlSiON compound has high wear resistance and high fracture resistance, and is more excellent in oxidation resistance than the TiAlN compound.

  In the sintered body according to the first embodiment, the first compound is Ti._(1-ab)Al_aSi _bO_xN_yContaining Ti_(1-ab)Al_aSi_bO_xN_yA, b, x and y in the formulas are 0.01 ≦ a ≦ 0.70, 0.01 ≦ b ≦ 0.55, 0.06 ≦ a + b ≦ 0.88, and 0.005 ≦ x ≦ 0. 6, 0.4 ≦ y ≦ 0.995 and 0.5 <x + y ≦ 1 are preferably satisfied. When the first compound includes a TiAlSiON compound that satisfies the above composition ratio, the sintered body can have higher oxidation resistance. The reason for this is as follows.

That is, the first compound comprises _{Ti (1-ab) Al a} Si b O x N y, Ti (1-ab) Al a Si b O x N a in _y, b, x and y are the above range, respectively As seen, the Al contained in the first compound forms a thermodynamically stable Al oxide film, and Si densifies the Al oxide film, so that the above-mentioned characteristics of the sintered body can be obtained. Further improve.

Further, a, b, x, and y in Ti _(1-ab) Al _a Si _b O _x N _y are 0.30 ≦ a ≦ 0.70, 0.10 ≦ b ≦ 0.20, 0, respectively. It is more preferable that 01 ≦ x ≦ 0.30 and 0.80 ≦ y ≦ 0.99 are satisfied. In this case, the above characteristics are remarkably improved.

  However, the content of the first compound in the sintered body according to the first embodiment is preferably 10% by volume or more and 100% by volume or less, more preferably 16% by volume or more, and 20% by volume or more. More preferably, it is more preferably 40% by volume or more, and particularly preferably 50% by volume or more. When content of the 1st compound in a sintered compact is less than 10 volume%, there exists a tendency for the said characteristic of a sintered compact to fall. This is considered to be due to an increase in the content of compounds, metals and the like other than the TiAlSiON compound in the sintered body.

  Moreover, it is preferable that the sintered compact which concerns on 1st Embodiment further contains 1 or more types selected from the group which consists of a 2nd compound, a 3rd compound, a 4th compound, and a 1st metal.

  The second compound is cubic boron nitride. The third compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O. The fourth compound is from the group consisting of Group 4 elements (Ti, Zr, Hf, etc.), Group 5 elements (V, Nb, Ta, etc.) and Group 6 elements (Cr, Mo, W, etc.) of the periodic table. A compound of one or more selected elements and one or more elements selected from the group consisting of B, C, N, and O. The first metal is one selected from the group consisting of Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, Ta, W, and Pb. It is a metal composed of the above.

  One or more types of sintered bodies selected from the group consisting of the second compound, the third compound, the fourth compound and the first metal (hereinafter, these are also referred to as “specific substances other than the first compound” for convenience) ) Are present at the interface between the first compounds. That is, the specific substance other than the first compound exists in the sintered body between the particles made of one first compound and the particles made of another first compound adjacent thereto.

  The presence of particles made of a substance other than the first compound at the interface of the particles made of the first compound causes the first compounds to be firmly bonded to each other. It will be excellent. This is because the sintered body containing the first compound and the second compound is composed of second particles (described later) serving as raw materials for the first compound and third particles serving as raw materials for other specific substances other than the first compound. In this case, a reaction product is generated at the interface between the second particle and the third particle during the sintering, and as a result, the first compound and This is because the second compound is firmly bonded.

  In addition, the sintered body contains a specific substance other than the first compound, so that in addition to the characteristic attributed to the characteristic of the first compound, the sintered body has a characteristic attributed to the specific substance other than the first compound. Can do. Therefore, by appropriately adjusting the composition of the specific substance other than the first compound, the sintered body can flexibly meet each need required for various cutting conditions.

  For example, when the sintered body contains cubic boron nitride (second compound), cubic boron nitride has an extremely high hardness, so that this sintered body has the second compound at the interface of the first compound. In addition to the improved fracture resistance, it can have high hardness due to having the second compound.

Specific examples of the third compound include borides such as SiB ₄ , aluminum boride (AlB ₁₂ ), carbides such as silicon carbide (SiC), aluminum nitride (AlN), and silicon nitride (Si ₃ N ₄ ). Examples thereof include oxides such as nitride, silicon oxide (SiO ₂ ), and aluminum oxide (Al ₂ O ₃ ).

Specific examples of the fourth compound include titanium boride (TiB ₂ ), zirconium boride (ZrB ₂ ), hafnium boride (HfB ₂ ), vanadium boride (VB), niobium boride (NbB ₂ ), boron Borides such as tantalum boride (TaB ₂ ), chromium boride (CrB ₂ ), molybdenum boride (MoB) and tungsten boride (WB). In addition, titanium carbide (TiC), zirconium carbide (ZrC), hafnium carbide (HfC), vanadium carbide (VC), niobium carbide (NbC), tantalum carbide (TaC), chromium carbide (Cr ₃ C ₂ ), molybdenum carbide ( And carbides such as Mo ₂ C) and tungsten carbide (WC). Further, titanium nitride (TiN), zirconium nitride (ZrN), hafnium nitride (HfN), vanadium nitride (VN), niobium nitride (NbN), tantalum nitride (TaN), chromium nitride (Cr ₂ N), molybdenum nitride (MoN) ) And a nitride composed of one metal element and nitrogen, such as tungsten nitride (WN).

Other specific examples of the fourth compound include titanium zirconium nitride (TiZrN), titanium hafnium nitride (TiHfN), titanium vanadium nitride (TiVN), titanium niobium nitride (TiNbN), titanium tantalum nitride (TiTaN), and titanium nitride. Chromium (TiCrN), titanium nitride molybdenum (TiMoN), titanium tungsten nitride (TiWN), zirconium nitride hafnium (ZrHfN), zirconium vanadium nitride (ZrVN), zirconium niobium nitride (ZrNbN), zirconium tantalum nitride (ZrTaN), zirconium nitride chromium (ZrCrN), zirconium molybdenum molybdenum (ZrMoN), zirconium tungsten nitride (ZrWN), hafnium vanadium nitride (HfVN), hafnium niobium nitride (Hf) bN), hafnium tantalum nitride (HfTaN), hafnium chromium nitride (HfCrN), hafnium molybdenum nitride (HfMoN), hafnium tungsten nitride (HfWN), vanadium niobium nitride (VNbN), vanadium tantalum nitride (VTaN), vanadium chromium nitride (VCrN) ), Vanadium nitride molybdenum (VMoN), vanadium tungsten nitride (VWN), niobium tantalum nitride (NbTaN), niobium chromium nitride (NbCrN), niobium molybdenum nitride (NbMoN), niobium tungsten nitride (NbWN), tantalum chromium nitride (TaCrN), Tantalum molybdenum nitride (TaMoN), tantalum tungsten nitride (TaWN), chromium molybdenum nitride (CrMoN), chromium tungsten nitride (CrWN), Such as fine molybdenum nitride chromium (MoWN), nitrides and the like consisting of two metal elements and nitrogen. In addition, titanium oxide (TiO ₂ ), zirconium oxide (ZrO ₂ ), hafnium oxide (HfO ₂ ), vanadium oxide (V ₂ O ₅ ), niobium oxide (Nb ₂ O ₅ ), tantalum oxide (Ta ₂ O ₅ ), Examples thereof include oxides such as Cr ₂ O ₃ ), molybdenum oxide (MoO ₃ ), and tungsten oxide (WO ₃ ).

Specific examples of the first metal include CoSi ₂ , Ti ₃ Al, TiAl, TiAl ₃ , TiSi ₂ , Ti ₅ Si ₃ , Ti ₅ Si ₄ , in addition to the simple metals listed above such as Co and Ni. An alloy such as TiSi or Ti ₃ Si may be used.

<< Second Embodiment >>
The tool according to the second embodiment is a tool using the sintered body according to the first embodiment. As described above, the sintered body containing the first compound composed of Ti, Al, Si, O, and N is excellent in properties such as hardness, fracture resistance, and oxidation resistance. It will be excellent in the characteristics.

  Examples of the tool according to the second embodiment may include an end mill, a cutting edge replacement cutting tip for milling, and a cutting edge replacement cutting tip for turning. Moreover, the whole tool may be comprised with the said sintered compact, and the one part (for example, blade edge | tip part) may be comprised with the said sintered compact.

  When the entire tool is made of the sintered body, the tool can be produced by processing the sintered body into a desired shape. Moreover, when a part of tool consists of the said sintered compact, a tool can be produced by joining a sintered compact to the desired position of the base | substrate which comprises a tool. The method for joining the sintered bodies is not particularly limited, but in order to firmly bond the base body and the sintered body between the base body and the sintered body from the viewpoint of suppressing the separation of the sintered body from the base body. It is preferable to interpose a bonding layer.

<< Third Embodiment >>
The method for manufacturing a sintered body according to the third embodiment includes a step of preparing first particles containing each element of Ti, Al, and Si (preparation step), and processing the first particles to obtain Ti, Al, A step (processing step) for producing second particles made of each element of Si, O, and N, and sintering the second particles to contain a first compound made of Ti, Al, Si, O, and N And a step of producing a body (sintering step). Moreover, the said process process is equipped with the process (heating process) of heating 1st particle | grains, and the process (rapid cooling process) of rapidly cooling the 1st particle | grains after a heating. Hereinafter, each process will be described with reference to FIGS. 1 and 2.

(Preparation process)
With reference to FIG. 1, first, in the preparation step of Step S <b> 1, first particles containing Ti, Al, and Si elements are prepared.

  1st particle | grains are raw material particles used as the raw material of a 1st compound. In particular, metal elements such as Ti, Al, and Si among Ti, Al, Si, O, and N constituting the first compound are supplied only from the first particles. For this reason, the first particles need to have at least the same composition ratio of Ti, Al, and Si as the composition of the first compound of interest. On the other hand, non-metallic elements such as O and N among Ti, Al, Si, O and N constituting the first compound are supplied from the first particles, and the atmosphere in the processing step described later (nitrogen atmosphere or the like) Can also be supplied. For this reason, the 1st particle does not necessarily need to have O and N equivalent to the composition of the 1st compound.

  By using one kind of raw material particles having a specific composition as the first particles, it is difficult to provide the target composition ratio of Ti, Al and Si in the first compound. What is necessary is just to use the 1st particle | grains with which the above raw material particles were mixed.

Examples of the raw material particles include particles made of one element such as Ti particles, Al particles, and Si particles, and particles made of two or three elements of Ti, Al, and Si. As the particles composed of the above two elements, Ti and Al particles such as Ti ₃ Al, TiAl, TiAl ₃ , Ti such as TiSi, Ti ₃ Si, TiSi ₂ , Ti ₅ Si ₃ , Ti ₅ Si ₄ , and Ti Examples thereof include particles made of Si and particles made of Al and Si such as an AlSi alloy. Examples of the particles composed of the above three elements include TiAlSi alloys.

Examples of the raw material particles include particles made of one or more nitrides, oxides, and oxynitrides selected from the group consisting of Ti, Al, and Si. Specifically, particles of Ti nitride, oxide or oxynitride such as TiN, TiO ₂ , TiO and TiON, Al nitride, oxide or oxynitride such as AlN, Al ₂ O ₃ and AlON And particles made of a material, particles of Si nitride such as Si ₃ N ₄ , SiO ₂ and SiON, particles made of oxide or oxynitride, SiAlON, Si ₂ Al ₃ O _{13 and the} like.

  In the case where raw material particles composed of two or more elements of Ti, Al, and Si are used as the raw material particles, first particles having a more uniform composition can be generated in the processing step described later. Further, when the raw material particles made of one or more nitrides, oxides, and oxynitrides selected from the group consisting of Ti, Al, and Si are used as the first particles, The amount of N and O to be applied can be easily adjusted.

  The average particle size of the first particles is preferably 10 μm or less. When the first particles having such a particle size are used, the reactivity between the particles can be further increased in the processing step described later, and particles containing a large amount of the second particles having the target composition can be produced. . In the present specification, the average particle diameter of particles refers to the median diameter based on the particle size distribution of particles measured by a known particle size distribution measurement method such as laser diffraction method.

  The first particles prepared in this step are preferably pressure-molded for use in the processing step described later. The method of pressure molding is not particularly limited, and a known method can be used.

(Processing process)
Next, in the processing step of step S2 in FIG. 1, the first particles are processed to produce second particles made of Ti, Al, Si, O, and N elements. This step includes a step of heating the first particles (heating step) and a step of rapidly cooling the first particles after heating (quenching step). This will be described with reference to FIG.

  Referring to FIG. 2, first, the first particles are heated in the heating process of step S <b> 21. By this heating step, a shortage of N in the first particles is imparted. The “shortage N” corresponds to the difference between the composition ratio of the nitrogen element in the first particles and the target composition ratio of the TiAlSiON compound in the first compound.

  In this heating step, the powder composed of the first particles or the molded body formed by pressure-molding the first particles is placed in a vacuum atmosphere, a nitrogen atmosphere, and an argon atmosphere. . The atmosphere in which the first particles are placed is appropriately selected depending on the composition of the first particles.

  For example, when the first particles contain O in addition to Ti, Al, and Si elements, and the O content satisfies the amount targeted in the first compound, the first particles are in an atmosphere containing nitrogen gas. Will be placed in. In addition, for example, when the first particles include N and O in addition to Ti, Al and Si elements, and the respective contents of N and O satisfy the amount targeted in the first compound, the first particles are Can be placed in an argon atmosphere or in a vacuum atmosphere.

  In addition, even if the first particles do not satisfy the amount of O targeted in the first compound because of the composition, the second particles may satisfy the amount of O targeted. This is known by the study of the present inventors. This is because there is oxygen adsorbed on the surface of the first particles, and this oxygen is taken into the first particles by the heating step, and the amount of oxygen reaches an amount that satisfies the insufficient amount of O.

  The heating temperature, atmospheric pressure, and partial pressure of each gas in the heating step are appropriately adjusted. For example, the heating temperature is preferably 1500 ° C. or higher, and the atmospheric pressure is preferably 0.1 atmospheric pressure or higher.

  Next, in the rapid cooling process of step S22, the powder composed of the first particles to which N and O are imparted by heating in the heating process, or the molded body of the first particles is cooled. Hereinafter, the powder composed of the first particles to which N and O have been imparted through the heating step, or the molded body of the first particles is referred to as a second particle precursor.

  The cooling rate of the second particle precursor in the rapid cooling step is at least larger than the cooling rate by furnace cooling, preferably 100 ° C./sec or more, and more preferably 200 ° C./sec or more. In addition, the cooling rate by furnace cooling is about 20 degrees C / min normally.

  By the rapid cooling step, second particles made of Ti, Si, Al, O and N can be obtained. Specifically, the second particles are composed of Ti, Si, Al, O and N, and all or most of the second particles are composed of a TiAlSiON compound. The composition ratio of the TiAlSiON compound contained in the second particles substantially matches the composition ratio of the TiAlSiON compound targeted for the first compound.

  In addition, when the said heating process and said rapid cooling process are performed using the molded object of a 1st particle, what is obtained after a rapid cooling process is a structure which consists of Ti, Al, Si, O, and N. The composition of this structure is the same as that of the second particles. In other words, since the structure is composed of the second particles, the second particles are obtained even when the structure is obtained in this way.

  The structure can be used as it is in the sintering step described later. However, in order to increase the sintering efficiency and perform uniform sintering, the structure is pulverized to form the second particles. It is preferable to obtain. This pulverization method is not particularly limited, and for example, a method of coarsely pulverizing by a known method and then further pulverizing by colliding a pulverizing medium with a vibration mill or a rotary mill can be adopted. Through this pulverization, granular second particles can be obtained.

  In the processing step of Step S2, as described above, the second particles can be obtained by continuously performing the heating step and the rapid cooling step. This is due to the following reason. That is, when the rapid cooling process is not continuously performed after the heating process, particles having a composition that does not satisfy the target composition tend to be generated. For example, when the first particles are heated using a heating furnace, and then the first particles after heating (second particle precursors) are simply cooled without being subjected to a rapid cooling step, the temperature of the heated first particles Will decline very slowly. In this case, Si or Al easily falls off from the TiAlSiON compound generated in the heating step, and as a result, particles that do not satisfy the targeted composition ratio in the first compound are generated. On the other hand, when the rapid cooling step is performed continuously after the heating step, such element escape can be effectively suppressed, and generation of particles having the unintended composition as described above can be suppressed. .

  As a method capable of continuously executing the heating step and the rapid cooling step as described above, (1) the first particles are heated in a reaction chamber under a desired atmosphere using a heat source such as a carbon heater, and then the atmospheric gas is changed. A method of introducing a cooling gas such as Ar after exhausting, (2) a method of burning and synthesizing the first particles in a reaction chamber under a desired atmosphere, and (3) a high temperature of the first particles in the reaction chamber under a desired atmosphere. Examples thereof include a method of passing through plasma.

Preferred conditions in the heating step when the method (1) is used are shown below. Also, the cooling rate can be set to 100 ° C./sec or more, and further to 200 ° C./sec or more.
Heating temperature: 1500 ° C. or more and 2000 ° C. or less Atmospheric pressure: 0.1 atm or more Heating time: 1 hour or more.

The preferable conditions in the heating step when the method (2) is used are shown below. The cooling rate can also be set to 100 ° C./min or more, and further can be set to 200 ° C./min or more.
Heating temperature: 2000 ° C. or more and 3000 ° C. or less Atmospheric pressure: 1.0 atm or more Heating time: 3 seconds or more.

Preferred conditions in the heating step when the method (3) is used are shown below. Also, the cooling rate can be set to 500 ° C./sec or more, and further can be set to 1000 ° C./sec or more.
Heating temperature: 2000 ° C. or more and 5000 ° C. or less Pressure: 0.1 atmosphere or more Heating time: 0.5 seconds or more.

  In addition, although 2nd particle | grains are produced by this process, when preparation of the 2nd particle | grains which have a desired composition is difficult by one execution of this process, you may perform this process repeatedly. In this case, it is not always necessary to repeat the same processing method. For example, the above steps (1) to (3) may be appropriately combined to execute this step.

(Sintering process)
Next, in the sintering step of step S3 in FIG. 1, the second particles are sintered to produce a sintered body containing the first compound composed of Ti, Al, Si, O, and N.

  The sintering of the second particles is preferably performed after the second particles are pressure-molded. Moreover, you may carry out simultaneously with pressure molding. Examples of methods for simultaneously performing pressure molding and sintering include a hot press (HP) method, a discharge plasma sintering (SPS) method, and an ultra-high pressure sintering method. Moreover, after shaping | molding by the cold isostatic pressing (CIP) method, it can also sinter using a hot isostatic pressing (HIP) method. In addition, you may use a normal pressure sintering method instead of the above pressure sintering methods.

  This step is preferably performed under an inert atmosphere in order to suppress the composition of the first compound in the sintered body from greatly changing from the composition of the second particles. The pressure during sintering is preferably 40 MPa or more and 20 GPa or less, and the temperature is preferably 1100 ° C. or more and 2500 ° C. or less. When the temperature at the time of sintering is less than 1100 ° C., the sintering tends to be insufficient, and a dense sintered body tends not to be obtained. When the temperature exceeds 2500 ° C., the first compound in the sintered body This is because there is a concern that the composition greatly changes from the composition of the second particles. The time required for the sintering varies depending on the amount (volume) of the second particles, the temperature, and the like. For example, when the sintering temperature is 1100 ° C. or higher and 2500 ° C. or lower, the time can be 15 minutes or longer.

  By performing the sintering step, the second particles are sintered, whereby a sintered body made of the first compound made of Ti, Al, Si, O and N can be obtained.

  According to the manufacturing method according to the third embodiment described in detail above, since a sintered body containing the first compound composed of Ti, Al, Si, O and N can be manufactured, high wear resistance and high A sintered body having defect resistance and high oxidation resistance can be provided. Moreover, the tool which consists of this sintered compact, or a tool using this sintered compact can be provided by cut | disconnecting the manufactured sintered compact by laser, wire discharge, etc. and processing it into a desired shape. .

<< Fourth Embodiment >>
As shown in FIG. 3, the method for manufacturing a sintered body according to the fourth embodiment includes a step of mixing the second particles and the third particles produced by the treatment step before the sintering step (mixing step). ) Is different from the third embodiment. Hereinafter, this mixing step will be described with reference to FIG. In addition, since the preparation process of step S31 in FIG. 3, the process process of step S32, and the sintering process of step S34 are the same as that of each of step S1-S3 of 3rd Embodiment, the description is not repeated.

(Mixing process)
Referring to FIG. 3, in the mixing step of step S33, the second particles obtained by the processing step of step S32 and the third particles having a composition different from that of the second particles are mixed.

  The third particles are particles composed of one or more selected from the group consisting of a fifth compound, a sixth compound, a seventh compound, and a second metal.

  The fifth compound is cubic boron nitride. The sixth compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O. Specifically, the sixth compound The compound similar to the 1st compound explained in full detail in embodiment is mentioned. The seventh compound is selected from the group consisting of one or more elements selected from the group consisting of Group 4 elements, Group 5 elements and Group 6 elements in the periodic table, and B, C, N, and O Specifically, the same compounds as the second compound described in detail in the first embodiment can be given. The second metal is one or more selected from the group consisting of Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, Ta, W, and Pb. Specifically, the same metal as the first metal described in detail in the first embodiment can be used.

In particular, the third particles preferably include cubic boron nitride. For example, when the third particles are made of cubic boron nitride, when the mixture of such third particles and second particles is sintered, most of the second compound becomes cubic boron nitride having excellent hardness. Further, when the third particles are made of cubic boron nitride, Si ₃ N ₄ can be present in the vicinity of the interface with the first compound in the second compound of the manufactured sintered body. In this case, both the particles (the particles made of the first compound and the particles made of the second compound) can be firmly bonded, and wear due to dropping of the particles can be reduced.

  In this step, it is preferable that the content of the third particles in the mixed particles of the second particles and the third particles is 90% by volume or less. When the content of the third particles exceeds 90% by volume, since the ratio of the first compound in the sintered body is too low, the effect derived from the first compound tends to be significantly reduced.

  More preferably, the content of the third particles in the mixed particles of the second particles and the third particles is 50% by volume or less. In particular, when the third particles include metal particles (particles composed only of metal elements), the content of the metal particles in the mixed particles is preferably 20% by volume or less. When the content of the metal particles in the mixed particles exceeds 20% by volume, the hardness of the manufactured sintered body tends to decrease.

  By performing the mixing step, a mixture composed of the second particles and the third particles is obtained. By sintering this in the sintering step of step S34, the sintering composed of the first compound and the second compound is performed. You can get a body.

  Here, in the present embodiment, most of the third particles are contained in the second compound while maintaining the composition thereof. That is, the composition of the third particles and the composition of the compound and / or metal contained in the second compound are almost the same. However, the second compound may contain a compound having a composition different from the composition of the third particles. This is because at the interface between the second particle and the third particle, a compound is generated by combining the element constituting the second particle and the element constituting the third particle.

  According to the manufacturing method according to the fourth embodiment described in detail above, a sintered body including a first compound composed of Ti, Al, Si, O, and N and a second compound having a composition different from that of the first compound. Can be manufactured. Such a sintered body can exhibit characteristics attributed to the second compound in addition to characteristics attributed to the first compound. Therefore, according to the manufacturing method according to the fourth embodiment, it is possible to provide a tool that has high wear resistance, high fracture resistance, and high oxidation resistance, and that meets various needs for cutting conditions.

  The present invention will be described more specifically with reference to examples and comparative examples. However, the present invention is not limited to these examples and comparative examples.

[Study 1]
By executing the above-described preparation process and processing process, second particles made of Ti, Al, Si, O, and N were produced and their characteristics were evaluated.

<< Examples 1 to 58 >>
(Preparation process)
As first particles, raw material particles in which raw material particles A, raw material particles B, and raw material particles C shown in Table 1 below were mixed were prepared. For example, in Example 1, Ti particles as raw material particles A, Al particles as raw material particles B, and Si particles as raw material particles C have a mixing ratio (raw material particles A: raw material particles B: raw material particles C). The first particles were prepared by mixing so that the mass ratio was 80:10:10. In addition, the average particle diameter of each 1st particle prepared in Examples 1-58 was as showing in Table 1. And the molded object which consists of 1st particle | grains was produced by pressure-molding each prepared 1st particle | grain.

(Processing process)
Next, a second particle composed of Ti, Al, Si, O, and N was produced by executing a treatment process using the produced compact. The processing steps in each example include (1) heating the first particles in a reaction chamber under a desired atmosphere using a heat source such as a carbon heater, and then exhausting the atmospheric gas, followed by cooling gas such as Ar. A method of introducing (shown as “gas quench” in Table 2), (2) a method of burning and synthesizing the first particles in a reaction chamber under a desired atmosphere (shown as “burning synthesis” in Table 2), and (3) Any method of passing one particle through a high temperature plasma in a reaction chamber under a desired atmosphere (shown as “high temperature plasma” in Table 2) was used. The conditions of the processing steps in each example are shown in Table 2 below.

  With reference to Table 2, the methods (1) to (3) will be specifically described using Examples 1, 8, and 11, respectively.

  The processing steps of Example 1 by the method (1) were performed as follows. First, the molded body was placed in a crucible having a gas supply part and a gas discharge part. Then, nitrogen gas was introduced into the crucible, the gas pressure in the crucible was set to 3 atm, and the inside of the crucible was heated at 1800 ° C. for 1 hour by a carbon heater arranged around the crucible. Thereby, the 1st particle of Example 1 was used for the heating process for 60 minutes at 1800 ° C under nitrogen atmosphere.

  After completion of the heating step, the atmosphere gas was evacuated by a vacuum pump, and then cooled by introducing Ar to 3 atm. The sample temperature was cooled to room temperature (25 ° C.) or lower. The cooling rate at this time was about 100 ° C./sec. Thereby, the 2nd particle precursor was used for the rapid cooling process, and the structure which consists of Ti, Al, Si, O, and N was obtained.

  Also in Examples 2-7, 16-18, and 36-39, the processing steps were performed in the same manner as in Example 1 except that various conditions were changed as shown in Table 2.

  The process of Example 8 by the method (2) was performed as follows. First, the molded body was placed in a pressure vessel having a gas supply part and a gas discharge part. Then, the pressure of the nitrogen gas in the pressure vessel was increased to 10 MPa (100 atm), and a part of the compact was heated using a heat source such as a tungsten filament to synthesize the first particles. The combustion time at this time was 15 seconds, and the heating temperature was 3000 ° C. Thereby, the first particles of Example 8 were subjected to a heating process at 3000 ° C. for 15 seconds in a nitrogen atmosphere.

  In combustion synthesis, since the heat source is only present at the time of ignition, the temperature in the pressure vessel immediately decreases after the combustion time has elapsed, and accordingly, the first particle (second particle precursor) after combustion synthesis is reduced. The temperature quickly dropped to room temperature. The cooling rate at this time was about 200 ° C./sec. Thereby, the 2nd particle precursor was used for the rapid cooling process, and the structure which consists of Ti, Al, Si, O, and N was obtained.

  In Examples 9, 10, 19-21, and 25-35, the treatment steps were performed in the same manner as in Example 8 except that various conditions were changed as shown in Table 2.

  The processing steps of Example 11 by the method (3) were performed as follows. First, while supplying nitrogen gas into the pressure vessel so that the gas pressure becomes 0.1 atm, high temperature plasma of 4500 ° C. is generated from the plasma generating electrode provided in the pressure vessel, and the first in the plasma. The particles were passed through. The processing time at this time was 1 second. Thereby, the first particles of Example 11 were subjected to a heating step at 4500 ° C. for 1 second in a nitrogen atmosphere.

  The cooling rate in the rapid cooling step after the heating step was about 1000 ° C./sec. Thereby, the 2nd particle precursor was used for the cooling process, and the structure which consists of Ti, Al, Si, O, and N was obtained. In addition, the rapid cooling process was continuously implemented when the heating process was completed.

  Also in Examples 12 to 15, 22 to 24, and 40 to 58, the processing steps were performed in the same manner as in Example 1 except that various conditions were changed as shown in Table 2.

<< Comparative Examples 1 and 2 >>
In Comparative Example 1, a powder made of TiN was produced, and in Comparative Example 2, a powder made of TiAlN was produced. Specifically, in Comparative Example 1, TiN (atomic ratio is 1: 0.97) particles having a particle size of 1 μm were prepared. In Comparative Example 2, AlTiN (atomic ratio: 0.5: 0.5: 1) particles having a particle size of 1 μm were prepared.

≪Characteristic evaluation of each particle≫
The composition of each particle of Examples 1 to 58 and the oxidation resistance of each particle of Examples 1 to 58 and Comparative Examples 1 and 2 were confirmed.

(composition)
Table 3 shows the contents (volume%) of the products (compounds) and TiAlSiON compounds contained in the second particles obtained in Examples 1 to 58. Among the contained products, the composition of compounds other than the TiAlSiON compound is identified by analyzing the cross section and surface of the particle with an XRD (X-ray diffraction) apparatus, and the composition of the TiAlSiON compound is EDX (energy dispersion). Type X-ray spectroscopy). Moreover, it processed so that the cross section of the obtained powder could be observed, the cross section of the powder was observed with the scanning electron microscope, and the TiSiAlON compound was discriminate | determined by the lightness and darkness of the color in powder. At that time, each compound was previously identified by elemental analysis. Furthermore, the visual field was binarized to quantify the TiSiAlON compound.

Regarding the column of “Product” in Table 3, for example, “TiAlSiON” indicates a TiAlSiON compound, and “Si ₃ N ₄ ” indicates a Si ₃ N ₄ compound. The composition of the TiAlSiON compound is described in the column “Ti _(1-ab) Al _a Si _b O _x N _y ”. Further, the content of the TiAlSiON compound is described in the column of “first compound content”.

Referring to Table 3, in Examples 1 to 58, it was confirmed that the sintered body was composed of the first compound containing the TiAlSiON compound. The TiAlSiON compound is Ti _(1-ab) Al _a Si _b O _x N _y (where a, b, x and y are 0.01 ≦ a ≦ 0.70 and 0.01 ≦ b ≦, respectively. It was also confirmed that 0.55, 0.06 ≦ a + b ≦ 0.88, 0.005 ≦ x ≦ 0.6, 0.4 ≦ y ≦ 0.995, and 0.5 <x + y ≦ 1 were satisfied.

(Oxidation resistance)
Each specimen was prepared by weighing 0.5 mg of each particle of Examples 1 to 58 and Comparative Examples 1 and 2. Each test specimen was subjected to differential thermal analysis while gradually raising the temperature from room temperature (25 ° C.) to 1400 ° C. in an air atmosphere. The lowest temperature at which the weight change of each specimen was confirmed was taken as the oxidation start temperature. The results of Examples 1 to 58 are shown in Table 3.

  With reference to Table 3, all the oxidation start temperature of each 2nd particle of Examples 1-58 was 460 degreeC or more. On the other hand, the oxidation start temperatures of the particles of Comparative Examples 1 and 2 were 400 ° C. and 450 ° C. In Table 3, the higher the “oxidation start temperature”, the better the oxidation resistance.

[Study 2]
The mixing step of mixing the second particles and the third particles, and the sintering step, each of the particles of Examples 1, 11 and 27 and the particles of Comparative Examples 1 and 2 are used as the second particles. Thus, a sintered body was produced and its characteristics were evaluated.

<< Examples 61 to 125 and Comparative Examples 3 to 6 >>
(Mixing process)
In Examples 61 to 125 and Comparative Examples 3 to 6, the mixing step was performed using the second particles and the third particles shown in Tables 4 and 5. Referring to Table 5, for example, in Example 61, the second particles prepared in Example 1 and the third particles made of cubic boron nitride (cBN) are mixed in a mixing ratio (second particles: third particles). Were mixed so that the volume ratio was 50:50 to prepare mixed particles.

(Sintering process)
Next, the obtained mixed particles were filled in a tantalum capsule, and were subjected to a sintering treatment using a press machine at the pressure, temperature, and sintering time shown in Tables 4 and 5 below.

  As described above, in Examples 61 to 125, sintered bodies containing the first compound and the second compound containing the TiAlSiON compound were obtained. Moreover, in Comparative Examples 3-6, the sintered compact containing the compound derived from 2nd particle | grains and the compound derived from 3rd particle | grains was obtained. Each sintered body had a disk shape with a diameter of 20 mm and a height of 1 mm.

≪Characteristic evaluation of each sintered body≫
It confirmed about the composition, abrasion resistance, and fracture resistance of each sintered compact of Examples 61-125 and Comparative Examples 3-6.

(composition)
Table 6 shows the contents (volume%) of products (compounds, metals) and TiAlSiON compounds contained in the sintered bodies obtained in Examples 61 to 125 and Comparative Examples 3 to 6, and the contents of TiN or TiAlN ( Table 7 shows the volume%). Among the contained products, the composition of compounds other than the TiAlSiON compound is identified by analyzing the cross section and surface of the sintered body with an XRD (X-ray diffraction) apparatus, and the composition of the TiAlSiON compound is EDX ( It was calculated by performing energy dispersive X-ray spectroscopy. Moreover, it processed so that the cross section of the obtained sintered compact could be observed, the cross section of the sintered compact was observed with the scanning electron microscope, and the TiSiAlON compound was discriminate | determined by the lightness and darkness of the color in a sintered compact. At that time, each compound was previously identified by elemental analysis. Furthermore, the visual field was binarized to quantify the TiSiAlON compound.

Regarding the column of “Product” in Tables 6 and 7, for example, “TiAlSiON” indicates a TiAlSiON compound, and “Si ₃ N ₄ ” indicates a Si ₃ N ₄ compound. The composition of the TiAlSiON compound is described in the column “Ti _(1-ab) Al _a Si _b O _x N _y ”. Further, the content of the TiAlSiON compound is described in the column of “first compound content”.

Referring to Table 6, in Examples 61 to 125, the sintered body contains a TiAlSiON compound, and the TiAlSiON compound is Ti _(1-ab) Al _a Si _b O _x N _y (where a, b, x and y is 0.01 ≦ a ≦ 0.70, 0.01 ≦ b ≦ 0.55, 0.06 ≦ a + b ≦ 0.88, 0.005 ≦ x ≦ 0.6, and 0.4 ≦ y, respectively. ≦ 0.995 and 0.5 <x + y ≦ 1 were confirmed, while the content of the TiAlSiON compound slightly decreased when converted from the mixing ratio of the second particles and the third particles. Many cases were seen.

  Therefore, although the composition of the second particles does not change before and after the sintering process, reaction products are generated at the interface due to the reaction with the third particles. Therefore, the mixing ratio is determined by the sintering process. It was thought that slight fluctuations were observed before and after. In addition, since the composition of the second particles does not change before and after firing, the TiAlSiON compound contained in the second particles and the TiAlSiON compound constituting the first compound are the same compound. Therefore, the oxidation resistance of the first compound Was found to depend on the oxidation resistance of the second particles.

  In addition, in the sintered bodies of Examples 61 to 125, products (compounds or metals) other than the TiAlSiON compound were included. Moreover, it was confirmed that products other than the TiAlSiON compound exist at the interface of the TiAlSiON compound.

(Abrasion resistance and fracture resistance)
The wear resistance and fracture resistance of the sintered bodies of Examples 61 to 125 and Comparative Examples 3 to 6 were evaluated by the following methods.

  First, each sintered body was processed using a laser to form a chamfer-shaped cutting tool having a chip shape of ISO model number CNGA120408, a cutting edge treatment of −25 °, and a width of 0.15 mm. Using each of the produced cutting tools, a cutting test was performed under the following cutting conditions, and the average flank wear amount (μm) and chipping amount (μm) of the cutting tool were measured. “Chipping” means a minute chipping generated in the cutting edge, and “chipping amount” means a chip width in the thickness direction of the cutting tool blade.

Work material: SCM415 hardened grooved steel (HRc58-62)
(Shape: A round bar with grooves of 2mm width at 1cm intervals)
Cutting speed: 100 m / min.
Feeding speed: 0.1mm / rev
Cutting depth: 0.1 mm
Cutting oil: None Cutting distance: 4 km.

  Each evaluation result is shown in Table 6 and Table 7. In Tables 6 and 7, the smaller the “flank wear amount”, the better the wear resistance. Also, the smaller the “chipping amount”, the better the chipping resistance.

  From Table 6 and Table 7, it turned out that the sintered compact of Examples 61-125 is excellent in characteristics, such as abrasion resistance and a fracture resistance, compared with the sintered compact of Comparative Examples 3-6. Further, when Example 110 and Example 118 were compared, the sintered body of Example 110 was superior in characteristics. This is considered to be because the content (volume%) of the mixed Co particles in Example 118 was large.

  The embodiments and examples disclosed herein are illustrative in all respects and should not be construed as being restrictive. The scope of the present invention is shown not by the above-described embodiment but by the scope of claims, and is intended to include meanings equivalent to the scope of claims and all modifications within the scope.

  The sintered body according to the present invention can be widely used for cutting tools. In particular, it can be suitably used for a cutting tool for cutting a work material having high hardness at a high temperature and a work material made of a heat-resistant alloy.

Claims (8)

  The sintered compact containing the 1st compound which consists of Ti, Al, Si, O, and N. The first compound includes Ti _(1-ab) Al _a Si _b O _x N _y ,
A, b, x, and y in the Ti _(1-ab) Al _a Si _b O _x N _y are 0.01 ≦ a ≦ 0.70, 0.01 ≦ b ≦ 0.55, and 0.06, respectively. The sintered body according to claim 1, satisfying ≦ a + b ≦ 0.88, 0.005 ≦ x ≦ 0.6, 0.4 ≦ y ≦ 0.995, and 0.5 <x + y ≦ 1.   The sintered body according to claim 1 or 2, wherein the content of the first compound in the sintered body is 10% by volume or more and 100% by volume or less. The sintered body further includes one or more selected from the group consisting of a second compound, a third compound, a fourth compound, and a first metal,
The second compound is cubic boron nitride;
The third compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O,
The fourth compound is selected from the group consisting of one or more elements selected from the group consisting of Group 4 elements, Group 5 elements and Group 6 elements in the periodic table, and B, C, N, and O A compound with one or more elements
The first metal is one or more selected from the group consisting of Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, Ta, W, and Pb. The sintered body according to any one of claims 1 to 3, wherein the sintered body is a metal made of   A tool using the sintered body according to any one of claims 1 to 4. Preparing a first particle containing each element of Ti, Al and Si;
Treating the first particles to produce second particles composed of Ti, Al, Si, O and N elements;
Sintering the second particles to produce a sintered body containing a first compound composed of Ti, Al, Si, O, and N, and
The step of producing the second particles includes
A method for manufacturing a sintered body, comprising: a step of heating the first particles; and a step of rapidly cooling the first particles after heating. Including the step of mixing the second particles and the third particles before the step of producing the sintered body,
The third particles are particles composed of one or more selected from the group consisting of a fifth compound, a sixth compound, a seventh compound and a second metal,
The fifth compound is cubic boron nitride;
The sixth compound is a compound of one or more elements of Al and Si and one or more elements selected from the group consisting of B, C, N, and O,
The seventh compound is selected from the group consisting of one or more elements selected from the group consisting of Group 4 elements, Group 5 elements and Group 6 elements in the periodic table, and B, C, N, and O A compound with one or more elements
The second metal is one selected from the group consisting of Ti, V, Cr, Mn, Co, Ni, Cu, Al, Sn, Si, Zr, Nb, Mo, Ag, Hf, Ta, W, and Pb. The manufacturing method of the sintered compact of Claim 6 which is a metal which consists of the above.   The method for producing a sintered body according to claim 7, wherein the mixing step is performed by setting the content of the third particles in the mixed particles of the second particles and the third particles to 90% by volume or less.

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